JPS581020A - Production of steel bar - Google Patents
Production of steel barInfo
- Publication number
- JPS581020A JPS581020A JP10033381A JP10033381A JPS581020A JP S581020 A JPS581020 A JP S581020A JP 10033381 A JP10033381 A JP 10033381A JP 10033381 A JP10033381 A JP 10033381A JP S581020 A JPS581020 A JP S581020A
- Authority
- JP
- Japan
- Prior art keywords
- steel bars
- steel
- strength
- tempering
- less
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/185—Hardening; Quenching with or without subsequent tempering from an intercritical temperature
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Articles (AREA)
Abstract
Description
【発明の詳細な説明】
この発明は高強度、高靭性で耐遅れ破壊性のすぐれた鋼
棒の製造方法に関するものである。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a method for manufacturing a steel bar with high strength, high toughness, and excellent delayed fracture resistance.
従来、２０ｗ４棒や高張力ボルトに使用される高強度、
高靭性材料は炭素を０．３０〜０，６０％程度含む材料
を焼入れ、焼戻ししたもの、たとえば、０．５％Ｃ鋼を
伸線によるサイズ合せ後、焼入焼もどししたもの、ある
いは０．６０−０．８０％Ｃの低合金）にライト南（た
とえば、（ｏ、７％Ｇ１１．２％Ｍｎｓ［）、７％ｃｒ
鋼 をγ相に加熱後空冷でパーライトにし、サイズ合
せした後ストレッチおよびブルーイング処理したものも
）が使われているが、これらの材料は抗張力が１’１０
〜１２０ ｋｇ／、ｌ、以上になるといずれも遅れ破壊
を起しやすいという欠点がある。High strength conventionally used for 20w4 rods and high tension bolts,
High-toughness materials include materials containing about 0.30 to 0.60% carbon that are quenched and tempered, such as 0.5% C steel that is sized by wire drawing and then quenched and tempered. 60 - 0.80% C low alloy) to light south (e.g. (o, 7% G 11.2% Mns[), 7% cr
Steel is heated to the γ phase, then air-cooled to pearlite, adjusted to size, then stretched and blued), but these materials have a tensile strength of 1'10.
When the weight exceeds 120 kg/l, the disadvantage is that delayed fracture is likely to occur.
この発明はこのような従来の欠点の解決のためになされ
たものであり、低炭素鋼に特定の処理を施すことにより
高強度、高靭性で耐遅れ破壊性のすぐれた鋼棒を製造で
きるようにしたものである。This invention was made to solve these conventional drawbacks, and by applying a specific treatment to low carbon steel, it is possible to manufacture steel bars with high strength, high toughness, and excellent delayed fracture resistance. This is what I did.
すなわち、この発明はｃ： ０．１０−０．３０％、Ｍ
ｎ ： ０．３０〜１．５％、Ｓｉ ： ０．８％以下
、Ｃｒ：１０％以下、Ｂ ： ０．０００５〜０．００
３０％ヲ含ミ、かつＴｉ：ｏ、０５％以下、Ｎｂ ：
［１，ｉ％以下、Ｖ二０．１％以下、Ａｄ：０．１％以
下の１種または２種以上およびその他不可避的に含まれ
る成分からなる−Ｈをフェライトとオーステナイト七の
２相誠に加熱して焼入れし、ついで高周波誘導加熱装置
により２００〜４００″Ｃの範囲に急速加熱焼戻しを行
なうようにしたものであり、これによって引張り強さ１
１０＆ｇ／−以上、絞り値５０％以上の鋼棒を得ようと
するものである。That is, this invention has c: 0.10-0.30%, M
n: 0.30-1.5%, Si: 0.8% or less, Cr: 10% or less, B: 0.0005-0.00
Contains 30%, Ti: o, 05% or less, Nb:
[-H consisting of 1, i% or less, V2 0.1% or less, Ad: 0.1% or less, and other unavoidably contained components, is added to the two phases of ferrite and austenite. It is heated and quenched, and then rapidly heated and tempered in the range of 200 to 400"C using a high-frequency induction heating device. This results in a tensile strength of 1.
The objective is to obtain a steel bar with a reduction of area of 10&g/- or more and a reduction of area of 50% or more.
炭素含有量を０．１０〜０．３０％に限定したのは、０
．１％以下では強度が不足し、０．３０％を越えると延
性が低下するからである。マンガンは脱酸等の溶製上０
．６０％以上が必要であり、また１、５０％を越えても
焼入性および固溶強化について１５％までの効果以上の
ものは得られない。シリコンは０，８％を越えると延性
が低下する。クロムは焼入性を向上さ。せるが、その効
果的な範囲は１．０％以下である。硼素はｏ、 ｏ ｏ
ｏ ｓ〜０．００３０％の範囲で低炭素鋼の焼入性に
顕著な効果を発揮する。The carbon content was limited to 0.10% to 0.30%.
．． This is because if it is less than 1%, the strength will be insufficient, and if it exceeds 0.30%, the ductility will decrease. Manganese is 0 in melting process such as deoxidation.
．． 60% or more is required, and even if it exceeds 1.50%, no effect greater than 15% on hardenability and solid solution strengthening will be obtained. When silicon exceeds 0.8%, ductility decreases. Chromium improves hardenability. However, its effective range is 1.0% or less. Boron is o, o o
It exhibits a remarkable effect on the hardenability of low carbon steel in the range of os to 0.0030%.
チタン、ニオブ、バナジウム、アルミニウムを含有させ
たのは鋼を細粒化させるため、および鋼中の窒素の存在
のために硼素の効果が減殺されるのを防止するためであ
り、また上記範囲を越えると炭化物の多量析出の問題が
生じるからである。The reason why titanium, niobium, vanadium, and aluminum are contained is to make the steel grain finer and to prevent the effect of boron from being diminished due to the presence of nitrogen in the steel. This is because if it exceeds the amount, the problem of large amounts of carbide precipitation will occur.
上記組成の材料を焼入れしてフェライトとマルテンサイ
トとめ２相組織にし、これを高周波誘導加熱によって焼
戻すことにより、耐遅れ破壊性を向上させることができ
る。従来は上記２相組織は靭性が劣るために鋼棒の用途
には不向きであると考えられていたが、以下に説明する
ように特定の焼戻し処理をすると靭性が改善されること
が解′った。Delayed fracture resistance can be improved by hardening a material having the above composition to form a two-phase structure of ferrite and martensite, and then tempering this by high-frequency induction heating. It was previously thought that the above-mentioned two-phase structure was unsuitable for steel bar applications due to its poor toughness, but it has now been discovered that toughness can be improved by applying a specific tempering treatment, as explained below. Ta.
上記の焼入れ操作は高周波誘導加熱によってフェライト
とオーステナイトとの２相域に急速に加熱して行なうこ
とが最適であるが、通常の加熱炉を用いても可能である
。ところで高周波誘導加熱装置による焼戻しでは、鋼棒
の表面部のみを焼戻しして°もよく、あるいは中心部よ
り表面部の方がより高温で焼戻しされるようにしてもよ
い。この焼戻し温度が２００ ’Ｃ未満のばあいは焼戻
し効果が不充分となって所定の強度、絞り（引張り強さ
１１０＃ｇ／−以上、絞り値５０％以上）が得られず、
また４ ０ Ｄ ’Ｃを越えると焼戻し軟化により強度
不足となる。The above-mentioned quenching operation is optimally carried out by rapid heating to a two-phase region of ferrite and austenite by high-frequency induction heating, but it is also possible to use a normal heating furnace. By the way, in tempering using a high-frequency induction heating device, only the surface portion of the steel bar may be tempered, or the surface portion may be tempered at a higher temperature than the center portion. If this tempering temperature is less than 200'C, the tempering effect will be insufficient and the desired strength and area of area (tensile strength of 110#g/- or more, reduction of area of 50% or more) will not be obtained.
Moreover, if it exceeds 40 D'C, the strength will be insufficient due to tempering softening.
焼戻し温度とその効果との関係を従来のマルテンサイト
１相鋼との比較で見ると、第３図に示すようになる。１
はマルテンサイト１相鋼、２はマルテンサイトとフェラ
イトとの２相鋼のそれぞれ焼医しによる抗張力の変化曲
線を示し、焼入れ体感Ａでは同一の抗張力であったもの
が２００〜４００ ’ｃの焼戻しをすることにより２相
鋼の方が抗張力が高くなることが示されている。６はマ
ルテンサイト１相鋼、４はマルテンサイトとフェライト
との２相鋼のそれぞれ焼戻しによる絞り値の変化曲線！
あり、このばあいも２００〜４００″Ｃの焼戻しにより
２相鋼では絞りが大きく改善されていることが示されて
いる。また２００℃未満では所定の強度、絞りが得られ
ず、４００′ｃを越えると焼戻し軟化により必要な強度
以下になる。The relationship between tempering temperature and its effect is shown in FIG. 3 in comparison with conventional martensitic single-phase steel. 1
1 shows the change curve of tensile strength due to quenching of martensite single-phase steel and 2 shows martensite and ferrite dual-phase steel, respectively.In quenching experience A, the same tensile strength was obtained by tempering of 200 to 400'c. It has been shown that duplex steel has higher tensile strength by doing so. 6 is a martensitic single-phase steel, and 4 is a martensite-ferrite dual-phase steel, each showing a change curve of the aperture value due to tempering!
In this case, it has been shown that tempering at 200 to 400"C greatly improves the reduction of area in duplex steel. Also, below 200°C, the required strength and reduction of area cannot be obtained, and tempering at 200 to 400"C If the strength exceeds the required strength, the strength will be lower than the required strength due to tempering softening.
第％１Ｗｔｔ焼戻し後の抗張力と絞りとの関係を従来の
マルテンサイト１相鋼との比較で見るト第４図に示すよ
うになる。５はマルテンサイト１相鋼の抗張力と絞りの
値を示す複数のデータのプロット群、６はマルテンサイ
トとフェライトとの２相鋼のプロット群を示し、両者は
焼戻し処理前は同一の抗張力のものを用いた。この図か
らも２相鋼のばあいは焼戻しにより抗張力および絞りの
特性が改善されることがわかる。The relationship between the tensile strength and the area of area after the %1 Wtt tempering is shown in FIG. 4 in comparison with a conventional martensitic single phase steel. 5 shows a plot group of multiple data showing the tensile strength and area of area of martensitic single phase steel, and 6 shows a plot group of martensite and ferrite dual phase steel, both of which have the same tensile strength before tempering treatment. was used. This figure also shows that in the case of duplex steel, the tensile strength and area of area characteristics are improved by tempering.
実施例
第１表に示す成分の直径９２譚肩の鋼棒を８５０でに５
分間加熱して水冷し、ついでこれを高周波誘導で！ｌ
５０ ’Ｃに急速加熱し、水冷した。Example: A steel rod with a diameter of 92 mm and the components shown in Table 1 was made into 850 mm.
Heat for a minute, cool with water, then use high frequency induction! l
Rapid heating to 50'C and water cooling.
上記焼入れ後の組織は第１図に示すようＧこなり、フェ
ライトとマルテンサイトとの容量比が約１：６の２相組
織となっている。これを３５０ ’ｃで焼戻すと第２図
に示すような組織になる′。〜また横断面の硬度は第５
図曲線７に示すようになり、外周部はど硬度が低くなっ
ている。これは高周波誘導加熱で急速加熱を行なってい
るため表面部がより強く焼戻されているからであり、こ
のように表面部を焼戻すと高強度でしかも耐遅れ破壊性
のすぐれた鋼棒が得られる。The structure after the above-mentioned quenching is a G-shaped structure as shown in FIG. 1, and is a two-phase structure with a capacity ratio of ferrite and martensite of about 1:6. When this is tempered at 350'c, it becomes the structure shown in Figure 2'. ~Also, the hardness of the cross section is 5th
As shown by curve 7 in the figure, the hardness of the outer peripheral portion is low. This is because the surface area is more strongly tempered due to rapid heating using high-frequency induction heating, and tempering the surface area in this way results in a steel bar with high strength and excellent delayed fracture resistance. can get.
また上記材料を７０℃、２０ｗｔ％のＮＨ４Ｎｏ。The above material was heated to 70°C and 20 wt% NH4No.
溶液中で９５ｋｇ／−の負荷応力をかけて応力腐食試験
を行なったところ、破断時間は３２時間となり、従来品
の同一抗張力を有する材料の破断時間（８時間）の４倍
となった。When a stress corrosion test was conducted in a solution by applying a load stress of 95 kg/-, the rupture time was 32 hours, which was four times the rupture time (8 hours) of a conventional material having the same tensile strength.
以上説明したように、この発明は特定の組成の低炭素鋼
を焼入れによってフェライトとマルテンサイトとの２相
組織にし、これを高周波誘導による加熱で表面部をより
強く焼戻ししたものであり、高強度、高靭性でしかも耐
遅れ破壊性のすぐれた鋼棒が得られるものである。そし
て、これによって得られた鋼棒はＰＣ鋼棒だけでなく、
ボルト材その地張力を付与されて使われる材料としてい
ずれも適用可能である。As explained above, the present invention is made by quenching low carbon steel with a specific composition to create a two-phase structure of ferrite and martensite, and then tempering the surface part more strongly by heating with high frequency induction, resulting in high strength. , a steel bar with high toughness and excellent delayed fracture resistance can be obtained. The steel rods obtained through this process are not only PC steel rods, but also
Any bolt material can be used as a material that is given tension.
第１図はこの発明による焼入れ後の断面組織写真、第２
図はそれを焼戻しした後の断面組織写真、第３図は焼戻
しの温度による特性の変化図、第４図は抗張力および絞
りのマルテンサイト１相鋼の比較図、第５図は硬度分布
図である。
２・・・マルテンサイトとフェライトとの２相鋼の抗張
力変化曲線、４・・・同２相鋼の絞り変化曲線、６・・
・同２相鋼の抗張力および絞り。
特許 出願人 神鋼ｍ線工業株式会社第 １ ？
第 ２ 図
）
第 ３ 図
潅ｆｌ（”ｃ）
第 ４ 図
第 ５ 図
手続補正書動式）
昭和５６年１２月ノア 日
特許庁長官 島 １）春 樹 殿 側部□″ 昭和５
６年特許願第１００３３３号 １、事件の表示
２、発明の名称
鋼棒の製造方法
３、補正をする者
事件との関係 特許出願人
名 称 神鋼鋼線工業株式会社
４、代理人
６、補正の対象
第 ｌ１１
１１１ｚ図Figure 1 is a photograph of the cross-sectional structure after quenching according to the present invention;
The figure shows a photograph of the cross-sectional structure after tempering, Figure 3 shows the change in properties depending on the tempering temperature, Figure 4 shows a comparison of martensitic phase 1 steel in terms of tensile strength and reduction of area, and Figure 5 shows a hardness distribution diagram. be. 2... Tensile strength change curve of martensite and ferrite dual phase steel, 4... Restriction change curve of the same dual phase steel, 6...
- Tensile strength and reduction of area of the same duplex steel. Patent Applicant: Shinko M-Line Industry Co., Ltd. No. 1? Figure 2) Figure 3 fl("c) Figure 4 Figure 5 Procedural amendment form) December 1980 Noah Japan Patent Office Commissioner Shima 1) Haruki-dono side □" 1978
6th Patent Application No. 100333 1. Indication of the case 2. Name of the invention Method for manufacturing steel bars 3. Relationship with the case by the person making the amendment Patent applicant name Title Shinko Wire Industry Co., Ltd. 4. Agent 6. Amendment Target number l11 111z figure
Claims (1)
０〜１．５％、Ｓｉ：０．８％以下、Ｏｒ：１．０％以
下、Ｂ：０、０００５〜０．００３０％を含み、かつＴ
１：０．０５％以下、Ｎｂ：０．１％以下、Ｖ ： ［
１，１％以下、Ａｄ：０．１％以下の１種または２種以
上およびその他不可避的に含まれる成分からなる鍔材を
フェライトとオーステナイトとの２相域に加熱して焼入
れし、ついで高周波誘導加熱装置により２００〜４００
’Ｃの範囲に急速加熱焼戻しを行なうことを特徴とす
る鋼棒の製造方法。1, C: 0.10-0.30%, Mn: 0.3
0 to 1.5%, Si: 0.8% or less, Or: 1.0% or less, B: 0,0005 to 0.0030%, and T
1: 0.05% or less, Nb: 0.1% or less, V: [
A flange material consisting of one or more types of 1.1% or less, Ad: 0.1% or less, and other unavoidably included components is heated and quenched to a two-phase region of ferrite and austenite, and then high-frequency 200-400 depending on induction heating device
A method for manufacturing a steel bar, characterized by performing rapid heating and tempering to a range of 'C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10033381A JPS581020A (en) | 1981-06-26 | 1981-06-26 | Production of steel bar |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10033381A JPS581020A (en) | 1981-06-26 | 1981-06-26 | Production of steel bar |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS581020A true JPS581020A (en) | 1983-01-06 |
Family
ID=14271213
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP10033381A Pending JPS581020A (en) | 1981-06-26 | 1981-06-26 | Production of steel bar |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS581020A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR20020084590A (en) * | 2001-05-03 | 2002-11-09 | 현대자동차주식회사 | Method for an automotive cylinder head bolt |
| CN103526117A (en) * | 2012-07-03 | 2014-01-22 | 广西柳工机械股份有限公司 | Non-quenched and tempered steel, engineering mechanical semiaxle manufactured by using same and manufacturing method of semiaxle |
| CN107254635A (en) * | 2017-06-26 | 2017-10-17 | 邢台钢铁有限责任公司 | It is a kind of to exempt from annealed alloy steel wire rod and its production method with excellent drawing property |
-
1981
- 1981-06-26 JP JP10033381A patent/JPS581020A/en active Pending
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR20020084590A (en) * | 2001-05-03 | 2002-11-09 | 현대자동차주식회사 | Method for an automotive cylinder head bolt |
| CN103526117A (en) * | 2012-07-03 | 2014-01-22 | 广西柳工机械股份有限公司 | Non-quenched and tempered steel, engineering mechanical semiaxle manufactured by using same and manufacturing method of semiaxle |
| CN107254635A (en) * | 2017-06-26 | 2017-10-17 | 邢台钢铁有限责任公司 | It is a kind of to exempt from annealed alloy steel wire rod and its production method with excellent drawing property |
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